CN107326315B - A kind of forging method producing the big specification Ti1350 alloy bar material of Φ 200mm or more - Google Patents

A kind of forging method producing the big specification Ti1350 alloy bar material of Φ 200mm or more Download PDF

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Publication number
CN107326315B
CN107326315B CN201710592008.5A CN201710592008A CN107326315B CN 107326315 B CN107326315 B CN 107326315B CN 201710592008 A CN201710592008 A CN 201710592008A CN 107326315 B CN107326315 B CN 107326315B
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forging
transition temperature
deformation
phase transition
fire time
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CN201710592008.5A
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Chinese (zh)
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CN107326315A (en
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黄德超
李超
彭晖
朱雪峰
詹孝冬
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湖南金天钛业科技有限公司
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    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22FCHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/16Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
    • C22F1/18High-melting or refractory metals or alloys based thereon
    • C22F1/183High-melting or refractory metals or alloys based thereon of titanium or alloys based thereon

Abstract

The invention discloses a kind of forging methods for producing the big specification Ti1350 alloy bar material of Φ 200mm or more, this method forges through cogging, intermediate forging and finished product forging, to obtain the good β class titanium alloy rod bar of each, intensity superelevation small to histological difference, fracture toughness.The present invention is based on monophase field upsetting pull deformation, and interts and deformed using two-phase section upsetting pull, individual fire time use flat upsetting pull mode of texturing, it can be improved the forging permeability of blank center portion, the β crystal boundary structure for obtaining distortion, it is continuous, straight to solve the problems, such as β crystal boundary, and controls the heating cycle and pass deformation of monophase field upsetting pull deformation, it is easy to get fine acicular α phase, can be improved the Fracture Toughness of material.

Description

A kind of forging method producing the big specification Ti1350 alloy bar material of Φ 200mm or more

Technical field

The present invention relates to titanium alloy forging technical fields, and in particular to a kind of preferable Φ of every structural homogenity of production The forging method of the big specification Ti1350 alloy bar material of 200mm or more.

Background technique

Ti1350 titanium alloy belongs to 1300MPa grades of high-strength light titanium alloy materials of intensity, and the country is in terms of the titanium alloy It studies still at an early stage, mature technology product there is no to can be used.The alloy material is production superhigh intensity aircaft configuration The critical material of part, room temperature tensile intensity can reach >=1350MPa, and have good fracture toughness, can substitute aircraft knot The part high-strength steel of structure, to the performance boost of aircraft, there are biggish meanings.The alloy belongs to nearly β class titanium alloy, and there are phases Temperature is low, and deformation tension is big, forges the feature of permeability difference.

Traditional monophase field cogging, the mode of texturing that the straight upsetting of two-phase section directly pulls out based on deformation can be encountered when producing this alloy Following difficulty: 1, the alloy transformation temperature about 840 DEG C, if with two-phase section upsetting pull deformation based on, can because alloy deformation drag greatly and Forge the deformation heat of the poor uncontrollable blank of permeability and each to histological difference;2, the fracture toughness that the alloy requires is higher, if Based on two-phase section upsetting pull deformation, two-phase section worked structure obtained is more difficult to be met the requirements.

Summary of the invention

In view of the deficiency of the prior art, the object of the present invention is to provide a kind of production Φ 200mm or more to advise greatly The forging method of lattice Ti1350 alloy bar material, it is good that this method can prepare each, intensity superelevation small to histological difference, fracture toughness β class titanium alloy rod bar.

To achieve the above object, the technical solution adopted by the present invention is that: a kind of big specification Ti1350 of production Φ 200mm or more The forging method of alloy bar material, comprises the following specific steps that:

Step 1, cogging forging:

By the ingot casting of Φ 680 ~ 780mm specification, deformation, road are pulled out in 200 ~ 400 DEG C of three upsettings three of progress more than β phase transition temperature Secondary Upsetting amount control is 30 ~ 45%;

Step 2, intermediate forging:

Step 2.1, the forging stock for completing step 1 carry out three secondary upsettings three of 2 ~ 4 fire for 100 ~ 300 DEG C more than beta transus temperature Deformation is pulled out, passage Upsetting amount is controlled 30 ~ 45%;

Step 2.2, the forging stock for completing step 2.1 carry out 2 fire time two upsettings of commutation for 50 ~ 100 DEG C more than β phase transition temperature Two pull out deformation, and passage Upsetting amount is controlled 40 ~ 45%;

Step 2.3, the forging stock for completing step 2.2 carry out the secondary upsetting one of 2 fire for 20 ~ 40 DEG C below β phase transition temperature Deformation is pulled out, passage Upsetting amount is controlled 30 ~ 40%;

Step 2.4, the forging stock for completing step 2.3 carry out two secondary upsettings of 2~4 fire for 30 ~ 50 DEG C more than β phase transition temperature Two pull out deformation, and passage Upsetting amount is controlled 40 ~ 45%;

Step 2.5, the forging stock for completing step 2.4 carry out the secondary flat of 2~4 fire for 30 ~ 50 DEG C more than β phase transition temperature Upsetting pull deformation, the control of passage Upsetting amount carry out big facet and exchange deformation pulling, final pulling is all directions base 40 ~ 45% Material;

Step 2.6, the forging stock for completing step 2.5 carry out the secondary upsetting one of 2 fire for 30 ~ 50 DEG C more than β phase transition temperature Deformation is pulled out, passage Upsetting amount is controlled 40 ~ 45%;

Step 2.7, the forging stock for completing step 2.6 carry out the secondary upsetting one of 2 fire for 20 ~ 40 DEG C below β phase transition temperature Deformation is pulled out, passage Upsetting amount is controlled 30 ~ 40%;

30 ~ 50 DEG C of pullings for carrying out 2 fire time more than β phase transition temperature of step 2.8, the forging stock for completing step 2.7 are forged It makes, Dan Huoci pulls out deformation amount controlling 30 ~ 40%;

Step 3, finished product forging

The forging stock that step 2 is completed 20 ~ 40 DEG C of pulling shapings for carrying out 1 fire time below β phase transition temperature are forged, Dan Huo Secondary deformation amount controlling is deformed into suitable specification 15 ~ 20%.

Steps 1 and 2, in 3, when blank shove charge, the above heating coefficient of β phase transition temperature be 0.2 ~ 0.7, β phase transition temperature with It is down 0.6 ~ 0.8;When the every fire time of blank heats, three sections of heating method is all used;After the completion of forging, air-cooled processing is carried out.

In steps 1 and 2, when being not particularly illustrated, all deformed using four square billets.

Compared with prior art, the beneficial effect that the present invention has is:

(1), the present invention is based on monophase field upsetting pull deformation, and interts and deformed using two-phase section upsetting pull, individual fire time uses Flat upsetting pull mode of texturing can be improved the forging permeability of blank center portion, obtain the β crystal boundary structure of distortion, solve β crystal boundary it is continuous, Straight problem ensure that the service performance of material;

(2), the present invention is easy to get fine acicular by the heating cycle and pass deformation of control monophase field upsetting pull deformation α phase can be improved the Fracture Toughness of material;

(3), the present invention by introduce commutation upsetting pull, the main deformation direction of blank can be adjusted in time, ensure that blank respectively to The uniformity of tissue.

Detailed description of the invention

Four width attached drawings are the high power figure for the Ti1350 alloy that the embodiment of the present invention one produces, and wherein Fig. 1 (1) is under 200X mirror T directional diagram, Fig. 1 (2) be 500X mirror under T directional diagram, Fig. 1 (3) be 200X mirror under L directional diagram, Fig. 1 (4) be 500X mirror Under L directional diagram.

Specific embodiment

Now in conjunction with specific embodiment, next the present invention is described in further detail.Obviously, therefore the present invention cannot be limited System is among the embodiment described range.Based on the embodiments of the present invention, those of ordinary skill in the art are not making wound Every other embodiment obtained under the premise of the property made is worked, is within the scope of protection of the invention.In following embodiments The method that actual conditions are not specified according to conventional methods and conditions, or is selected according to product manual.

Embodiment one (forging process of 350 ㎜ scale rod bar of Φ)

Step 1, cogging forging:

680 ~ 780mm of Φ specification, about 2.5 tons of ingot casting are heated to 800 DEG C using electric furnace, 2~4h is preheated, slowly heats up 200 ~ 400 DEG C more than to β phase transition temperature, after carrying out 5~7h heat preservation, three upsettings three is carried out using 40/45MN quick forging machine and pull out deformation, It is required that jumping-up speed control, in 10 ~ 20mm/s, for the control of passage Upsetting amount 30 ~ 45%, finally pulling is four square billets;

Step 2, intermediate forging:

Step 2.1, the forging stock for completing step 1 are heated to 800 DEG C, preheat 2~4h, are slowly warming up to β phase transition temperature Above 100 ~ 300 DEG C, after carrying out 5~7h heat preservation, deformation, jumping-up speed are pulled out using three upsettings three that 40/45MN quick forging machine carries out 2 fire time Degree control is in 10 ~ 20mm/s, and for the control of passage Upsetting amount 30 ~ 45%, finally pulling is four square billets;

Step 2.2, the forging stock for completing step 2.1 are heated to 800 DEG C, preheat 2~4h, are slowly warming up to β phase transition temperature Du or more 50 ~ 100 DEG C, carry out 5~7h heat preservation after, using 40/45MN quick forging machine carry out 2 fire time two upsettings two of commutation pull out deformation, Jumping-up speed control is in 10 ~ 20mm/s, and for the control of passage Upsetting amount 40 ~ 45%, finally pulling is four square billets;

Step 2.3, the forging stock for completing step 2.2 are heated to 750 DEG C, preheat 2~4h, are slowly warming up to β phase transition temperature 20 ~ 40 DEG C below degree, after carrying out 5~7h heat preservation, deformation, jumping-up speed are pulled out using the upsetting one that 40/45MN quick forging machine carries out 2 fire time Degree control is in 5 ~ 10mm/s, and for the control of passage Upsetting amount 30 ~ 40%, finally pulling is all directions base;

Step 2.4, the forging stock for completing step 2.3 are heated to 800 DEG C, preheat 2~4h, are slowly warming up to β phase transition temperature Du or more 30 ~ 50 DEG C, after carrying out 5~7h heat preservation, pull out deformation using two upsettings two that 40/45MN quick forging machine carries out 2 fire time, jumping-up is fast Degree control in 10 ~ 20mm/s, the control of Upsetting amount 40 ~ 45%, finally pulling for 500~600 × 700~900 × 1100~ The square billet of 1200 ㎜;

Step 2.5, the forging stock for completing step 2.4 are heated to 800 DEG C, preheat 2~4h, are slowly warming up to β phase transition temperature Du or more 30 ~ 50 DEG C, carry out 5~7h heat preservation after, using 40/45MN quick forging machine carry out 4 fire time flat upsetting pulls deform, jumping-up speed Degree control is in 10 ~ 20mm/s, and for the control of passage Upsetting amount 40 ~ 45%, finally pulling is all directions base;

Step 2.6, the forging stock for completing step 2.5 are heated to 800 DEG C, preheat 2~4h, are slowly warming up to β phase transition temperature Du or more 30 ~ 50 DEG C, after carrying out 5~7h heat preservation, pull out deformation using the upsettings one that 40/45MN quick forging machine carries out 2 fire time, jumping-up is fast Degree control is in 10 ~ 20mm/s, and for the control of passage Upsetting amount 40 ~ 45%, finally pulling is all directions base;

Step 2.7, the forging stock for completing step 2.6 are heated to 750 DEG C, preheat 2~4h, are slowly warming up to β phase transition temperature 20 ~ 40 DEG C below degree, after carrying out 5~7h heat preservation, deformation, jumping-up speed are pulled out using the upsetting one that 40/45MN quick forging machine carries out 2 fire time Degree control is in 5 ~ 10mm/s, and for the control of passage Upsetting amount 30 ~ 40%, finally pulling is four square billets;

Step 2.8, the forging stock for completing step 2.7 are heated to 800 DEG C, preheat 2~4h, are slowly warming up to β phase transition temperature Du or more 30 ~ 50 DEG C, carry out 4~7h heat preservation after, using 40/45MN quick forging machine carry out 2 fire time pullings deform, Dan Huoci pulling For deformation amount controlling 30 ~ 40%, finally pulling is all directions base;

Step 3, finished product forging:

The forging stock that step 2 is completed is heated to 750 DEG C, preheats 1~3h, is slowly warming up to β phase transition temperature or less 20 ~ 40 DEG C, after carrying out 3~5h heat preservation, using 40/45MN quick forging machine, 1 fire time pulling shaping is carried out on flat anvil or wrestling and is forged to about 350 ㎜ scale rod bar of Φ, Dan Huoci pull out deformation amount controlling 15 ~ 20%.

It is respectively smaller to histological difference, room temperature tensile is strong through 350 ㎜ scale rod bar of Ti1350 alloy Φ made from above-mentioned steps Degree >=1350MPa, fracture toughness >=60 the results are shown in Table 1, Fig. 1 (1), Fig. 1 (2), Fig. 1 (3), Fig. 1 (4).

Table: the results of property of Ti1350 alloy Φ 350mm scale rod bar

The present invention innovates on the basis of the forging technology of conventional beta class titanium alloy large size bar, and the tissue of acquisition is each It is smaller to difference, solve the problems, such as that β crystal boundary is continuous, straight.

Claims (5)

1. a kind of forging method for producing the big specification Ti1350 alloy bar material of Φ 200mm or more, which is characterized in that including having as follows Body step:
Step 1, cogging forging:
By the ingot casting of Φ 680 ~ 780mm specification, deformation, passage upsetting are pulled out in 200 ~ 400 DEG C of three upsettings three of progress more than β phase transition temperature Thick deformation amount controlling is 30 ~ 45%;
Step 2, intermediate forging:
Step 2.1, by forging stock that step 1 is completed, change is pulled out in 100 ~ 300 DEG C of three upsettings three for carrying out 2 ~ 4 fire time more than beta transus temperature Shape, passage Upsetting amount are controlled 30 ~ 45%;
Forging stock that step 2.1 is completed is carried out 2 fire time two upsettings two of commutation and pulled out for 50 ~ 100 DEG C by step 2.2 more than β phase transition temperature Deformation, passage Upsetting amount are controlled 40 ~ 45%;
Step 2.3, by forging stock that step 2.2 is completed, change is pulled out in 20 ~ 40 DEG C of upsettings one for carrying out 2 fire time below β phase transition temperature Shape, passage Upsetting amount are controlled 30 ~ 40%;
Step 2.4, by forging stock that step 2.3 is completed, 30 ~ 50 DEG C of two upsettings two for carrying out 2~4 fire time are pulled out more than β phase transition temperature Deformation, passage Upsetting amount are controlled 40 ~ 45%;
Step 2.5, the forging stock for completing step 2.4 carry out the secondary flat upsetting pull of 2~4 fire for 30 ~ 50 DEG C more than β phase transition temperature Deformation, the control of passage Upsetting amount carry out big facet and exchange deformation pulling, final pulling is all directions blank 40 ~ 45%;
Step 2.6, by forging stock that step 2.5 is completed, change is pulled out in 30 ~ 50 DEG C of upsettings one for carrying out 2 fire time more than β phase transition temperature Shape, passage Upsetting amount are controlled 40 ~ 45%;
Step 2.7, by forging stock that step 2.6 is completed, change is pulled out in 20 ~ 40 DEG C of upsettings one for carrying out 2 fire time below β phase transition temperature Shape, passage Upsetting amount are controlled 30 ~ 40%;
30 ~ 50 DEG C of pullings for carrying out 2 fire time more than β phase transition temperature of step 2.8, the forging stock for completing step 2.7 are forged, single Fiery pulling deformation amount controlling is 30 ~ 40%;
Step 3, finished product forging
The forging stock that step 2 is completed 20 ~ 40 DEG C of pulling shapings for carrying out 1 fire time below β phase transition temperature are forged, and Dan Huoci becomes Shape amount is controlled 15 ~ 20%, is deformed into suitable specification.
2. the forging method of the big specification Ti1350 alloy bar material of production Φ 200mm or more according to claim 1, feature It is, steps 1 and 2, in 3, when blank shove charge, the above heating coefficient of β phase transition temperature is 0.2 ~ 0.7, β phase transition temperature or less It is 0.6 ~ 0.8.
3. the forging method of the big specification Ti1350 alloy bar material of production Φ 200mm or more according to claim 1, feature It is, steps 1 and 2, in 3, when the every fire time heating of blank, all uses three sections of heating method;After the completion of forging, air-cooled place is carried out Reason.
4. the forging method of the big specification Ti1350 alloy bar material of production Φ 200mm or more according to claim 1, feature It is, ingot casting or forging stock in 3, are first heated to 800 DEG C before carrying out upsetting pull deformation, preheat 2~4h by steps 1 and 2.
5. the forging method of the big specification Ti1350 alloy bar material of production Φ 200mm or more according to claim 1, feature It is, in steps 1 and 2 .1,2.2,2.4,2.5,2.6, jumping-up speed control is in 10 ~ 20mm/s;Step 2.3, in 2.7, jumping-up speed Degree control is in 5 ~ 10mm/s.
CN201710592008.5A 2017-07-19 2017-07-19 A kind of forging method producing the big specification Ti1350 alloy bar material of Φ 200mm or more CN107326315B (en)

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CN102641978B (en) * 2012-05-17 2014-06-11 湖南金天钛业科技有限公司 Method for processing TC18 titanium alloy large-sized section bar
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